CN114096490B - Reinforced glass plate and method for manufacturing same - Google Patents
Reinforced glass plate and method for manufacturing same Download PDFInfo
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- CN114096490B CN114096490B CN202080046654.1A CN202080046654A CN114096490B CN 114096490 B CN114096490 B CN 114096490B CN 202080046654 A CN202080046654 A CN 202080046654A CN 114096490 B CN114096490 B CN 114096490B
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- glass sheet
- tempered glass
- glass plate
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- 239000011521 glass Substances 0.000 title claims description 249
- 238000000034 method Methods 0.000 title claims description 31
- 238000004519 manufacturing process Methods 0.000 title claims description 22
- 239000005341 toughened glass Substances 0.000 claims abstract description 134
- 238000005496 tempering Methods 0.000 claims abstract description 11
- 230000035882 stress Effects 0.000 claims description 118
- 238000005728 strengthening Methods 0.000 claims description 38
- 238000010521 absorption reaction Methods 0.000 claims description 34
- 238000003426 chemical strengthening reaction Methods 0.000 claims description 29
- 230000003014 reinforcing effect Effects 0.000 claims description 25
- 150000003839 salts Chemical class 0.000 claims description 20
- 230000008569 process Effects 0.000 claims description 16
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 14
- 238000005520 cutting process Methods 0.000 claims description 14
- 230000005484 gravity Effects 0.000 claims description 13
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 9
- 230000002787 reinforcement Effects 0.000 claims description 9
- 230000008646 thermal stress Effects 0.000 claims description 7
- 239000011241 protective layer Substances 0.000 claims description 6
- 239000000126 substance Substances 0.000 abstract description 6
- 238000009826 distribution Methods 0.000 description 20
- 239000006058 strengthened glass Substances 0.000 description 12
- 238000005342 ion exchange Methods 0.000 description 10
- 239000000463 material Substances 0.000 description 10
- 238000013001 point bending Methods 0.000 description 9
- FGIUAXJPYTZDNR-UHFFFAOYSA-N potassium nitrate Chemical compound [K+].[O-][N+]([O-])=O FGIUAXJPYTZDNR-UHFFFAOYSA-N 0.000 description 9
- 238000012360 testing method Methods 0.000 description 8
- 239000005345 chemically strengthened glass Substances 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 230000001678 irradiating effect Effects 0.000 description 7
- 238000004031 devitrification Methods 0.000 description 6
- 150000002500 ions Chemical class 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 230000001681 protective effect Effects 0.000 description 5
- 238000006124 Pilkington process Methods 0.000 description 4
- 238000005452 bending Methods 0.000 description 4
- 238000011156 evaluation Methods 0.000 description 4
- 230000009477 glass transition Effects 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 239000005340 laminated glass Substances 0.000 description 4
- 238000005259 measurement Methods 0.000 description 4
- 238000010583 slow cooling Methods 0.000 description 4
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 239000000835 fiber Substances 0.000 description 3
- 230000010355 oscillation Effects 0.000 description 3
- 235000010333 potassium nitrate Nutrition 0.000 description 3
- 239000004323 potassium nitrate Substances 0.000 description 3
- 239000011347 resin Substances 0.000 description 3
- 229920005989 resin Polymers 0.000 description 3
- 239000002344 surface layer Substances 0.000 description 3
- 239000002390 adhesive tape Substances 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 230000000452 restraining effect Effects 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- 238000004227 thermal cracking Methods 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 description 1
- YCKRFDGAMUMZLT-UHFFFAOYSA-N Fluorine atom Chemical compound [F] YCKRFDGAMUMZLT-UHFFFAOYSA-N 0.000 description 1
- 229910018068 Li 2 O Inorganic materials 0.000 description 1
- 239000004677 Nylon Substances 0.000 description 1
- 238000001069 Raman spectroscopy Methods 0.000 description 1
- QAOWNCQODCNURD-UHFFFAOYSA-L Sulfate Chemical compound [O-]S([O-])(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-L 0.000 description 1
- 239000003513 alkali Substances 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000003373 anti-fouling effect Effects 0.000 description 1
- 239000011449 brick Substances 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000007495 chemical tempering process Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000003280 down draw process Methods 0.000 description 1
- 239000000428 dust Substances 0.000 description 1
- 229910052731 fluorine Inorganic materials 0.000 description 1
- 239000011737 fluorine Substances 0.000 description 1
- 239000012943 hotmelt Substances 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 239000011229 interlayer Substances 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 230000031700 light absorption Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000003595 mist Substances 0.000 description 1
- 239000006060 molten glass Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229920001778 nylon Polymers 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 229910052700 potassium Inorganic materials 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
- 239000004065 semiconductor Substances 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 239000005361 soda-lime glass Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C23/00—Other surface treatment of glass not in the form of fibres or filaments
- C03C23/0005—Other surface treatment of glass not in the form of fibres or filaments by irradiation
- C03C23/0025—Other surface treatment of glass not in the form of fibres or filaments by irradiation by a laser beam
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/04—Glass compositions containing silica
- C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
- C03C3/083—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound
- C03C3/085—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal
- C03C3/087—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal containing calcium oxide, e.g. common sheet or container glass
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B27/00—Tempering or quenching glass products
- C03B27/02—Tempering or quenching glass products using liquid
- C03B27/03—Tempering or quenching glass products using liquid the liquid being a molten metal or a molten salt
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B33/00—Severing cooled glass
- C03B33/09—Severing cooled glass by thermal shock
- C03B33/091—Severing cooled glass by thermal shock using at least one focussed radiation beam, e.g. laser beam
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C17/00—Surface treatment of glass, not in the form of fibres or filaments, by coating
- C03C17/28—Surface treatment of glass, not in the form of fibres or filaments, by coating with organic material
- C03C17/32—Surface treatment of glass, not in the form of fibres or filaments, by coating with organic material with synthetic or natural resins
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C21/00—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface
- C03C21/001—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C21/00—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface
- C03C21/001—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions
- C03C21/002—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions to perform ion-exchange between alkali ions
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/04—Glass compositions containing silica
- C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
- C03C3/083—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B2201/00—Type of glass produced
- C03B2201/06—Doped silica-based glasses
- C03B2201/30—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi
- C03B2201/54—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi doped with beryllium, magnesium or alkaline earth metals
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C2218/00—Methods for coating glass
- C03C2218/30—Aspects of methods for coating glass not covered above
- C03C2218/355—Temporary coating
Landscapes
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Engineering & Computer Science (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Geochemistry & Mineralogy (AREA)
- General Chemical & Material Sciences (AREA)
- Life Sciences & Earth Sciences (AREA)
- Physics & Mathematics (AREA)
- Optics & Photonics (AREA)
- Health & Medical Sciences (AREA)
- Toxicology (AREA)
- Thermal Sciences (AREA)
- Surface Treatment Of Glass (AREA)
- Glass Compositions (AREA)
Abstract
The present invention relates to a tempered glass sheet having a first main surface, a second main surface opposite to the first main surface, and an end surface, wherein at least one of the first main surface and the second main surface has a surface compressive stress formed by a chemical tempering treatment, the tempered glass sheet has a tempered portion in which a planar compressive stress is formed along the end surface in a direction parallel to the end surface, the maximum value of the planar compressive stress of the tempered portion is 1MPa to 120MPa, and the width of the tempered portion from the end surface in a normal direction of the end surface is 0.5 times or more the thickness of the tempered glass sheet.
Description
Technical Field
The present invention relates to a tempered glass sheet and a method for manufacturing the same.
Background
There is known a strengthened glass plate in which compressive stress is formed on a main surface of the glass plate and tensile stress is formed inside the glass plate in order to improve the strength of the glass plate. The tempered glass includes a physically tempered glass obtained by heating a glass plate and quenching the glass plate to thereby form a temperature difference between a main surface and an inside thereof; the chemically strengthened glass is obtained by immersing a glass plate in molten salt and performing ion exchange between ions having a small ion radius on the main surface side and ions having a large ion radius on the molten salt side.
Since the chemically strengthened glass plate has a larger compressive stress layer formed on the principal surface than the physically strengthened glass plate, it is resistant to sudden impact, and thus has been used for protective glass for wristwatches, and has been used for protective glass for smart phones and the like in recent years. Patent document 1 proposes a chemically strengthened glass sheet used as a building window, an outer wall, a solar cell protective glass, or a vehicle window.
Prior art literature
Patent literature
Patent document 1: international publication No. 2014/168446
Disclosure of Invention
Problems to be solved by the invention
The chemically strengthened glass plate has a strong resistance to impact on the main surface on one side and a weak resistance to impact on the end surface on the other side, and is easily broken when a defect such as a crack is generated on the end surface.
The invention provides a strengthened glass plate with strong strength of main surface and end surface and less breakage and a manufacturing method thereof.
Means for solving the problems
The tempered glass plate of the present invention has a first main surface, a second main surface opposite to the first main surface, and an end surface, wherein,
at least one of the first major face and the second major face has a surface compressive stress formed by a chemical strengthening treatment,
The tempered glass plate has a tempered portion in which a planar compressive stress is formed along the end face in a direction parallel to the end face,
the maximum value of the plane compressive stress of the reinforcement part is 1MPa to 120MPa, and
the width of the reinforcing portion from the end face in the direction normal to the end face is 0.5 times or more the thickness of the reinforced glass plate.
The method for producing a tempered glass sheet of the present invention is a method for producing a tempered glass sheet, which comprises:
a chemical strengthening treatment step in which at least one main surface of a glass sheet is immersed in a molten salt, thereby forming a surface compressive stress on the main surface of the glass sheet; and
an end face strengthening step of forming a plane compressive stress along an end face of the glass plate in a direction parallel to the end face after the chemical strengthening treatment step, and
in the end face strengthening process, the glass plate is heated so that:
the temperature T1 of the glass plate at a position above the strain point of the glass plate, the temperature T2 of the end face being less than the softening point of the glass plate and T1 > T2,
The position is a position at which a length from the end face in a normal direction of the end face is the same as a thickness of the tempered glass sheet.
Effects of the invention
The tempered glass plate of the present invention has high strength on both the main surface and the end surface, and is not easily broken.
Drawings
Fig. 1 is a perspective view of a tempered glass sheet according to an embodiment of the present invention.
Fig. 2 is a plan view of a tempered glass sheet according to an embodiment of the present invention.
Fig. 3 (a) is a cross-sectional view of a tempered glass sheet according to an embodiment of the present invention, fig. 3 (B) is a plan view of a tempered glass sheet according to an embodiment of the present invention, and fig. 3 (C) shows a relationship between a distance from an end surface and a plane compressive stress in a parallel direction in the tempered glass sheet according to an embodiment of the present invention.
Fig. 4 is a cross-sectional view of a tempered glass sheet when laser light is irradiated in an end face tempering process.
Fig. 5 is a cross-sectional view showing a tempered glass plate of an embodiment.
Fig. 6 shows weibull diagrams for examples 1 and 2.
Detailed Description
Hereinafter, a tempered glass sheet according to an embodiment of the present invention will be described in detail with reference to the accompanying drawings.
Fig. 1 is a perspective view of a tempered glass sheet according to an embodiment of the present invention, fig. 2 is a plan view of the tempered glass sheet according to an embodiment of the present invention, fig. 3 (a) is a cross-sectional view of the tempered glass sheet according to an embodiment of the present invention, and fig. 3 (B) is a plan view of the tempered glass sheet according to an embodiment of the present invention. Fig. 3 (C) is a graph showing a relationship between a distance from an end surface and a plane compressive stress in the tempered glass sheet according to the embodiment of the present invention.
The tempered glass sheet 10 according to one embodiment of the present invention is a tempered glass sheet having a first main surface 11a, a second main surface 11b opposite to the first main surface 11a, and an end surface 12, wherein at least one of the first main surface 11a and the second main surface 11b has a surface compressive stress formed by a chemical tempering treatment, the tempered glass sheet has a tempered portion 30, a plane compressive stress is formed in the tempered portion 30 along the end surface 12 in a direction parallel to the end surface 12, the maximum value of the plane compressive stress of the tempered portion 30 is 1MPa to 120MPa, and a width C of the tempered portion 30 from the end surface 12 in a normal direction of the end surface 12 is 0.5 times or more of a thickness T of the tempered glass sheet.
The tempered glass sheet 10 of one embodiment of the present invention is suitable for use as, for example, a building window, an outer wall, a handrail material, a solar cell protective glass, a vehicle window. As the building window, a window of a house, a building, or the like can be exemplified.
The tempered glass sheet according to one embodiment of the present invention can be used as a single glass for various applications such as building windows, outer walls, armrest materials, solar cell protection glass, and vehicle windows. In another embodiment, the laminated glass may be used as laminated glass obtained by bonding 2 or more glass plates with an interlayer film.
In another embodiment, 2 or more glass sheets may be arranged at intervals to be used as a multiple glass. In another embodiment, the glass sheet may be coated on the surface thereof.
In the laminated glass and the laminated glass structure, at least one or more of the reinforced glass sheets of the present invention may be used.
At least one of the principal surfaces 11a and 11b of the tempered glass sheet 10 according to one embodiment of the present invention is subjected to a chemical strengthening treatment to form a surface compressive stress, and it is preferable that both of the principal surfaces 11a and 11b are subjected to a chemical strengthening treatment to form a surface compressive stress.
As will be described later, the tempered glass sheet 10 according to one embodiment of the present invention is formed by immersing a preheated glass sheet in a molten salt, for example, a heated potassium nitrate molten salt, subjecting the glass surface layer, for example, na and K in the molten salt to ion exchange, and subjecting the glass surface layer to a chemical tempering treatment, whereby a surface compressive stress is formed in at least one of the main surfaces 11a, 11 b. Therefore, the Na amount of the main surfaces 11a, 11b on which the surface compressive stress is formed is smaller than the Na amount of the inside of the tempered glass plate 10.
In the tempered glass sheet 10 according to the embodiment of the present invention, the surface compressive stress value (hereinafter, also referred to as CS) of the surface compressive stress in at least one of the first main surface 11a and the second main surface 11b is preferably 200MPa or more. If CS is 200MPa or more, the mechanical strength of the tempered glass plate is high, and thus it is preferable. CS is more preferably 250MPa or more, still more preferably 300MPa or more, particularly preferably 350MPa or more, and most preferably 380MPa or more.
On the other hand, in at least one of the first main surface 11a and the second main surface 11b, CS of the surface compressive stress is preferably 1200MPa or less. If CS is 1200MPa or less, the internal tensile stress is less likely to be extremely high. In addition, the chemical strengthening treatment step can be immersed in the molten salt at a high temperature for a short time, and the strengthened glass plate 10 can be easily obtained. In addition, when the tempered glass sheet 10 is cut, a cutting line generated by the wheel blade chopper is easily formed. CS is more preferably 800MPa or less, still more preferably 500MPa or less, particularly preferably 480MPa or less, and most preferably 460MPa or less. Here, CS, which is the surface compressive stress, is a value measured at the center of gravity of the first main surface 11a or the second main surface 11 b.
In the tempered glass sheet 10 according to one embodiment of the present invention, the depth (hereinafter also referred to as DOL) of the surface compressive stress in the sheet thickness direction is preferably 5 μm or more in at least one of the first main surface 11a and the second main surface 11 b. If DOL is 5 μm or more, sufficient strength can be obtained and impact resistance can be achieved. The DOL is more preferably 10 μm or more, still more preferably 20 μm or more, particularly preferably 30 μm or more, and most preferably 40 μm or more.
On the other hand, DOL of the surface compressive stress is preferably 100 μm or less. If DOL is 100 μm or less, the immersion in the molten salt can be performed for a short time, and the tempered glass plate 10 can be easily obtained. The DOL is more preferably 80 μm or less, still more preferably 60 μm or less, particularly preferably 50 μm or less. Here, DOL of the surface compressive stress is a value measured at the center of gravity of the first main surface 11a or the second main surface 11 b.
Here, CS and DOL can be measured using a surface stress meter.
The tempered glass sheet 10 according to an embodiment of the present invention may not form surface compressive stress generated by the chemical tempering treatment on the end face 12. As described later, the glass sheet 10 in which no surface compressive stress is formed on the end face 12 can be obtained by cutting the glass sheet after the chemical strengthening treatment. The tempered glass sheet 10 manufactured by such a method can be manufactured by performing a tempering treatment on a large glass sheet and then cutting the glass sheet into a used size, and thus productivity is good.
The chamfer 50 may be provided at the boundary between the end face 12 and the first main face 11a and the boundary between the end face 12 and the second main face 11 b. By providing the chamfer 50 on the end face 12, the corner of the tempered glass sheet 10 is less likely to be damaged when the tempered glass sheet 10 is being manufactured in various applications such as building windows, outer walls, armrest materials, solar cell protection glass, and vehicle windows. Examples of the type of chamfer of the end face 12 include C chamfer, R chamfer, a combination of R chamfer and C chamfer, and the like. The chamfer shape of the end face 12 may be linear or curved. The end face 12 may be an end face obtained by polishing after chamfering. The machining damage generated during chamfering can be removed by grinding. The end face 12 may also be formed by: after scribing with the thermal stress of the laser, gas burner, the glass sheet is cut so that microcracks generated when the glass sheet is cut are not generated. The end face 12 is formed by grinding and cutting after thermal stress scribing, and scattering of laser beams in an end face strengthening step described later can be reduced.
The tempered glass sheet 10 according to one embodiment of the present invention has a tempered portion 30, and a planar compressive stress is formed in the tempered portion 30 along the end face 12 in a direction parallel to the end face 12. The width C of the reinforcing portion 30 in the normal direction of the end face 12 from the end face 12 is 0.5 times or more the thickness T of the reinforced glass plate. By providing the end face 12 with the reinforcing portion 30 having a width C that is 0.5 times or more the thickness T of the tempered glass sheet, the planar compressive stress becomes stronger than the tensile stress generated in the end face 12 when the temperature distribution is generated in the tempered glass sheet 10, and defects such as cracks are less likely to occur in the end face 12, and the tempered glass sheet 10 is less likely to break.
The width C of the reinforced portion is preferably 0.7 times or more, more preferably 1.0 times or more, further preferably 1.5 times or more, and particularly preferably 2.0 times or more the thickness T of the reinforced glass plate 10. The upper limit of the width C of the reinforcing portion is not particularly limited, but may be 5.0 times or less, 4.0 times or less, or 3.0 times or less the thickness T of the reinforced glass sheet 10 in order to reduce the influence of the plane tensile stress generated at the position 40 adjacent to the reinforcing portion 30 in the direction parallel to the end face 12 on the opposite side to the end face 12.
Here, the deflection stress was measured in the vertical direction of the first main surface 11a and the second main surface 11b by a birefringence two-dimensional distribution evaluation device. The bias stress is a plane stress, and when the bias stress in the direction parallel to the end face 12 is a compressive plane stress, the bias stress in the direction parallel to the end face 12 is a tensile plane stress. The width C of the reinforced portion is the shortest distance between the edges of the main surfaces 11a and 11b and the position where the measured plane compressive stress is 0 in the main surfaces 11a and 11b of the reinforced glass sheet 10.
The reinforcement portion 30 may not be formed at the corner 13 where the adjacent end surfaces 12 contact each other. The distance G from the corner 13 where the adjacent end surfaces 12 contact each other to the reinforcing portion 30 may be 1.0 to 10 times the thickness T of the reinforced glass sheet 10.
Here, in the case where the corner 13 of the tempered glass sheet 10 is chamfered without the corner 13, the distance from the corner where virtual extension surfaces of adjacent end surfaces 12 contact each other to the strengthening portion 30 may be 1.0 times or more and 10 times or less the thickness T of the tempered glass sheet 10.
The maximum value of the plane compressive stress of the strengthening portion 30 of the strengthened glass plate 10 according to one embodiment of the present invention is 1MPa to 120MPa. If the maximum value of the plane compressive stress of the reinforcement portion 30 is 1MPa or more, the mechanical strength of the end face 12 is high. The maximum value of the plane compressive stress of the reinforcement portion 30 is more preferably 2MPa or more, still more preferably 3MPa or more, and particularly preferably 5MPa or more. If the maximum value of the plane compressive stress of the reinforcing portion 30 is 120MPa or less, the plane tensile stress generated at the position 40 of the reinforcing portion 30 adjacent to the opposite side of the end face 12 does not become too strong, and the reinforced glass sheet 10 is not easily broken even if damage occurs to the main faces 11a, 11b of the reinforced glass sheet 10. The maximum value of the plane compressive stress of the reinforcement portion 30 may be 100MPa or less, 50MPa or less, 30MPa or less, or 20MPa or less. Here, the maximum value of the plane compressive stress is the maximum value of the plane compressive stress of the strengthened portion measured on one principal surface of the strengthened glass plate 10 by the birefringent two-dimensional distribution evaluation device, and is the value shown in fig. 3 (C).
The tempered glass sheet 10 according to one embodiment of the present invention preferably does not have a planar tensile stress in the strengthening portion 30. The strengthened glass sheet 10 is less likely to thermally crack because the strengthening portion 30 does not have a planar tensile stress.
The tempered glass sheet 10 according to an embodiment of the present invention may have a protective layer formed on the end face 12. Examples of the protective layer include: adhesive tape, ultraviolet curable resin, and hot melt resin.
The tempered glass sheet 10 according to one embodiment of the present invention preferably has areas of the first main surface 11a and the second main surface 11b, respectively0.001m 2 The above. If the area is 0.001m 2 The above is suitable for various applications such as building windows, outer walls, solar cell protection glass, and vehicle windows. The areas of the first main face 11a and the second main face 11b may be 0.1m, respectively 2 The above may be 1m 2 The above may be 2m 2 Above, it may be 3m 2 The above may be 5m 2 The above may be 7m 2 Above, 9m may also be used 2 The above.
On the other hand, the areas of the first main surface 11a and the second main surface 11b are preferably 12m, respectively 2 The following is given. If the area is 12m 2 In the following, the handling of the tempered glass sheet is facilitated, and breakage due to contact with the peripheral member when the tempered glass sheet is installed can be suppressed, for example. The area can be 10m 2 The following is given.
The tempered glass sheet 10 according to one embodiment of the present invention preferably has a rectangular first main surface 11a and a rectangular second main surface 11 b. If rectangular, it is easy to provide for example as a building window, an outer wall, a handrail material, a solar cell protection glass. Here, the rectangle is substantially a rectangular quadrangle, and when the distance from any one side to the opposite side is measured, errors in the measured positions of the long side and the short side are each within 0.3%, including shapes in which corners have curvature, cutouts, and the like.
In the case where the tempered glass sheet 10 according to the embodiment of the present invention is rectangular, the length b of the long sides of the first main surface 11a and the second main surface 11b may be 50mm or more, may be 100mm or more, may be 300mm or more, may be 500mm or more, may be 1000mm or more, may be 2000mm or more, and may be 2500mm or more. The length b of the long sides of the first main surface 11a and the second main surface 11b may be 5000mm or less. Here, the length b of the long side refers to the shortest distance b between the two opposing short sides shown in fig. 2.
In the case where the tempered glass sheet 10 according to the embodiment of the present invention is rectangular, the length a of the short sides of the first main surface 11a and the second main surface 11b may be 5mm or more, may be 10mm or more, may be 50mm or more, may be 100mm or more, may be 500mm or more, may be 1000mm or more, and may be 2000mm or more. The length a of the short sides of the first main surface 11a and the second main surface 11b may be 3000mm or less. Here, the length a of the short side refers to the shortest distance a between two opposite long sides shown in fig. 2.
The tempered glass sheet 10 according to one embodiment of the present invention may have a sheet thickness of 0.5mm or more from the viewpoints of strength, workability, and the like. The thickness may be 1mm or more, 2mm or more, 3mm or more, or 5mm or more. On the other hand, if the plate thickness is 25mm or less, the weight is light, and thus it is preferable. The thickness is more preferably 22mm or less, and still more preferably 19mm or less.
The weight of the tempered glass sheet 10 according to one embodiment of the present invention is preferably 1000kg or less. If the weight is 1000kg or less, the weight is light, and thus it is preferable. The weight is more preferably 500kg or less. In addition, the weight is preferably 2kg or more from the viewpoint of strength and the like. The weight is more preferably 5kg or more, and still more preferably 10kg or more.
In addition, the tempered glass sheet 10 according to one embodiment of the present invention may have a functional film such as a heat ray reflection film or an antifouling film formed on one or both of the first main surface 11a and the second main surface 11 b.
The glass transition temperature Tg of the tempered glass sheet 10 according to one embodiment of the present invention is preferably 530 ℃. This suppresses relaxation of the surface compressive stress during ion exchange. The glass transition temperature Tg is more preferably 540℃or higher.
The specific gravity of the tempered glass sheet 10 according to one embodiment of the present invention is preferably 2.45 to 2.55.
The terms "to" representing the above-mentioned numerical ranges are used in the meaning of the lower limit value and the upper limit value inclusive of the numerical values described before and after the term "to" is used in the same meaning in the present specification unless otherwise specified.
The tempered glass sheet 10 according to one embodiment of the present invention preferably has a uniform specific gravity throughout the tempered glass sheet 10. The uniform specific gravity of the entire tempered glass sheet 10 means that the difference between the specific gravity of the portion from the end face 12 of the tempered glass sheet 10 to the depth of 1/10 or less of the sheet thickness and the specific gravity of the portion from the main faces 11a, 11b at the centers of the main faces 11a, 11b to the depth of 1/10 or less of the sheet thickness is within a range of-0.50% to 0.00% relative to the specific gravity of the portion from the main faces 11a, 11b at the centers of the main faces 11a, 11b to the depth of 1/10 or less of the sheet thickness of the tempered glass sheet 10. The specific gravity can be estimated by measuring the surface virtual temperature by any method such as raman spectroscopy.
The Young's modulus of the tempered glass plate 10 according to one embodiment of the present invention is preferably 65GPa or more. This makes the rigidity and breaking strength sufficient. The Young's modulus may be 70GPa or more. On the other hand, if the Young's modulus is 90GPa or less, embrittlement of the tempered glass sheet is suppressed, and chipping of the tempered glass sheet during cutting and dicing can be suppressed. The Young's modulus may be 85GPa or less, or 80GPa or less.
The tempered glass plate 10 according to one embodiment of the present invention preferably has an average thermal expansion coefficient of 30×10 in the range of 50 to 350 ℃ -7 At least 140×10 per DEG C -7 And/or lower. If the average thermal expansion coefficient is 30X 10 in the range of 50-350 DEG C -7 When the laser beam 60 is irradiated in an end surface strengthening step described later, the strengthening portion 30 can be formed even if the temperature T2 of the end surface of the glass plate 10 is less than the softening point of the glass plate 10. The average thermal expansion coefficient in the range of 50℃to 350℃is more preferably 60X 10 -7 At least 80X 10, more preferably at least -7 At least 85X 10, particularly preferred is a temperature of at least/DEG C -7 And/or higher. In addition, if the average thermal expansion coefficient is 140X 10 in the range of 50 to 350 DEG C -7 If the temperature difference between the irradiated portion and the non-irradiated portion of the laser beam 60 is generated by the irradiation of the laser beam 60 in the end face strengthening step, the stress generated will not become excessive, and the strengthened glass plate 10 will not be easily broken. The average thermal expansion coefficient in the range of 50℃to 350℃is more preferably 100X 10 -7 Preferably 95X 10 or less at a temperature of/DEG C -7 And/or lower.
Here, the tempered glass sheet 10 according to one embodiment of the present invention preferably contains, in terms of mole percent on an oxide basis: 0.003 to 1.5 percent of Fe 2 O 3 、56％～75% SiO 2 0 to 20 percent of Al 2 O 3 8 to 22 percent of Na 2 O, 0-10% of K 2 O, mgO of 0-14% and ZrO of 0-5% 2 And 0 to 12% CaO. Hereinafter, unless otherwise specified, percentages refer to the contents in terms of mole percentages based on oxides.
The reason why the glass composition of the tempered glass sheet 10 according to one embodiment of the present invention is limited to the above-described range will be described below.
When near infrared laser is used for end face processing described later, it is preferable that Fe is contained 2 O 3 . Fe in glass 2+ The ion absorbs the laser beam with the wavelength of 1000 nm-1100 nm. If Fe is 2 O 3 If the content of (2) is 0.003% or more, the end face can be efficiently heated by the laser beam. Fe (Fe) 2 O 3 The content of (2) is more preferably 0.005% or more, still more preferably 0.01% or more, particularly preferably 0.02% or more, and most preferably 0.05% or more. If Fe is 2 O 3 If the content of (2) is 1.5% or less, the laser beam is not easily absorbed by the glass surface and is easily condensed inside the glass. Fe (Fe) 2 O 3 The content of (c) is more preferably 1.0% or less, still more preferably 0.5% or less, still more preferably 0.3% or less, particularly preferably 0.2% or less, and most preferably 0.1% or less.
In the case of using a laser beam other than near infrared rays, it is preferable that an appropriate absorption component is contained in an appropriate amount in the glass according to the wavelength of the laser beam. Since glass is colored by absorption of light having a wavelength in the visible light region, colored glass can be used for end face strengthening by a visible light laser.
SiO 2 SiO as a component for forming a network structure in a glass microstructure 2 Is the main component of the glass. SiO (SiO) 2 The content of (2) is preferably 56% or more, more preferably 63% or more, still more preferably 66% or more, particularly preferably 68% or more. In addition, siO 2 The content of (2) is preferably 75% or less, more preferably 73% or less, and still more preferably 72% or less. When SiO 2 When the content of (C) is 56% or more, the glassThe stability and weather resistance of the glass are improved. On the other hand, when SiO 2 When the content of (C) is 75% or less, it is advantageous in terms of meltability and moldability.
Al 2 O 3 Not essential, but Al 2 O 3 Has the effect of improving ion exchange performance in chemical strengthening, especially increasing CS, and therefore can contain Al 2 O 3 . In addition, al 2 O 3 The weather resistance of the glass is improved. In the presence of Al 2 O 3 In the case of (1), al 2 O 3 The content of (2) is preferably 0.4% or more, more preferably 0.6% or more, and still more preferably 0.8% or more. In addition, the refractive index becomes low, and the reflectance becomes low. In addition, when Al 2 O 3 When the content of (b) is 20% or less, the devitrification temperature does not greatly increase even when the viscosity of the glass is high, and therefore, the glass is advantageous in melting and molding in a soda lime glass production line. Al (Al) 2 O 3 The content of (2) is more preferably 10% or less, still more preferably 5% or less, particularly preferably 3% or less, and most preferably 2% or less.
SiO 2 And Al 2 O 3 The sum of the contents (hereinafter, also referred to as SiO 2 +Al 2 O 3 Content) is preferably 68% or more. When SiO 2 +Al 2 O 3 When the content is 68% or more, chipping resistance at the time of forming an indentation is improved. In addition, the refractive index becomes low, and the reflectance becomes low. SiO (SiO) 2 +Al 2 O 3 The content is more preferably 70% or more. In addition, siO 2 +Al 2 O 3 The content is preferably 80% or less. When SiO 2 +Al 2 O 3 When the content is 80% or less, the viscosity of the glass at high temperature is reduced and the glass is easily melted. SiO (SiO) 2 +Al 2 O 3 The content is more preferably 76% or less, and still more preferably 74% or less.
Na 2 O is a component that forms surface compressive stress by ion exchange, and has an effect of deepening DOL. In addition, na 2 O is a component that reduces the high-temperature viscosity and devitrification temperature of the glass and improves the meltability and formability of the glass. Na (Na) 2 The content of O is preferably 8% or more, more preferably 10% or more, and still more preferably 12% or more. In addition, na 2 The content of O is preferably 22% or less, more preferably 16% or less, and further preferably 14% or less. When Na is 2 When the O content is 8% or more, a desired surface compressive stress is easily formed by ion exchange. On the other hand, when Na 2 When the content of O is 22% or less, sufficient weather resistance can be obtained.
K 2 O may contain K because of its effect of increasing ion exchange rate and deepening DOL 2 O. On the other hand, when K 2 If O is too large, a sufficient CS cannot be obtained. In the presence of K 2 In the case of O, K 2 The content of O is preferably 10% or less, more preferably 2% or less, and further preferably 1% or less. When K is 2 When the O content is 10% or less, a sufficient CS can be obtained.
MgO is not indispensable, but is a component for stabilizing glass. In the case of containing MgO, the content of MgO is preferably 2% or more, more preferably 4% or more, and still more preferably 6% or more. The MgO content is preferably 14% or less, more preferably 10% or less, and even more preferably 8% or less. When the MgO content is 2% or more, the chemical resistance of the glass becomes good. The meltability at high temperature becomes good, and devitrification is not easily caused. On the other hand, when the MgO content is 14% or less, devitrification is not likely to occur, and a sufficient ion exchange rate can be obtained.
ZrO 2 In order to reduce the refractive index and reduce the reflectance, the composition for increasing the refractive index preferably contains substantially no ZrO 2 . In the present specification, "substantially free" means that the material is not contained, i.e., not intentionally contained, except for unavoidable impurities mixed from the material or the like. However, zrO 2 As a result of having the effect of increasing CS of the chemically strengthened glass, zrO may be contained 2 . In the presence of ZrO 2 In the case of ZrO 2 The content of (2) is preferably 5% or less, more preferably 3% or less, and still more preferably 1% or less.
CaO is a component for stabilizing glass, although it is not essential. When CaO is contained, the content of CaO is preferably 2% or more, more preferably 5% or more, and still more preferably 7% or more. The CaO content is preferably 12% or less, more preferably 10% or less, and even more preferably 9% or less. When the CaO content is 2% or more, chemical resistance becomes good. In addition, when the CaO content is 12% or less, a sufficient ion exchange rate can be maintained, and a desired DOL can be obtained.
Although not essential, srO may be contained in order to reduce the high temperature viscosity of the glass and to reduce the devitrification temperature. Since SrO has an effect of reducing ion exchange efficiency, it is preferable that SrO is not contained, particularly when DOL is to be increased. When SrO is contained, the SrO content is preferably 3% or less, more preferably 2% or less, and still more preferably 1% or less.
Although not essential, baO may be contained in order to reduce the high-temperature viscosity of the glass and to reduce the devitrification temperature. Since BaO has an effect of increasing the specific gravity of the glass, baO is preferably not contained in the case of the light weight. When BaO is contained, the BaO amount is preferably 3% or less, more preferably 2% or less, and further preferably 1% or less.
Since ZnO is reduced in the float furnace to form product defects when a glass sheet is formed by the float process, znO is preferably substantially not contained.
In addition, sulfate, chloride, fluoride, and the like may be appropriately contained as a refining agent for melting glass.
The tempered glass sheet of the present invention essentially contains the above-described components, but may contain other components within a range that does not impair the object of the present invention. When such components are contained, the total content of these components is preferably 5% or less, more preferably 3% or less, and typically 1% or less. Hereinafter, the other components will be described by way of example.
In order to improve the meltability or glass strength at high temperature, B may be contained in a range of less than 1% 2 O 3 . Typically, when both contain Na 2 O or K 2 Alkali component of O and B 2 O 3 During volatilization, the bricks are significantly eroded, and therefore preferably substantially free of B 2 O 3 。
Li 2 O is a component that tends to cause stress relaxation by lowering the strain point, and as a result, stable surface compressive stress cannot be obtained, and therefore, it is preferable that Li is not contained 2 O, even when Li is contained 2 In the case of O, the content is also preferably 1% or less, more preferably 0.05% or less, and particularly preferably 0.01% or less.
Next, a method for manufacturing the tempered glass sheet 10 according to an embodiment of the present invention will be described.
In the case of manufacturing the tempered glass sheet 10 according to one embodiment of the present invention, the glass sheet manufacturing process, the chemical tempering process, and the end surface tempering process are performed.
In the glass sheet production process, for example, various raw materials are appropriately prepared, heated to about 1400 ℃ to 1800 ℃ and melted, homogenized by defoaming, stirring, etc., formed into a plate shape by a known float method, a downdraw method, a roll method, a press method, etc., slowly cooled, and cut into a desired size, thereby producing a glass sheet.
In the chemical strengthening treatment step, at least one main surface of the obtained glass sheet is immersed in a molten salt, and a desired surface compressive stress is formed on the main surface. The chemical strengthening treatment process comprises a preheating process, a chemical strengthening process and a slow cooling process.
In the preheating step, the glass plate is preheated before the chemical strengthening treatment. Preheating is carried out, for example, by: the glass plate is placed into an electric furnace at normal temperature, the electric furnace is heated to a preheating temperature, and the glass plate is kept for a certain time. In order to prevent breakage due to thermal shock in the chemical strengthening process, the glass sheet may be kept at the preheating temperature for a certain period of time after the temperature rise is completed. The holding time is preferably 10 minutes or more, more preferably 20 minutes or more, still more preferably 30 minutes or more, and particularly preferably 40 minutes or more.
In the chemical strengthening treatment step, the preheated glass plate is immersed in a molten salt, for example, a heated potassium nitrate molten salt, and Na in the glass surface layer is ion-exchanged with K in the molten salt. In the present invention, the molten potassium nitrate salt includes, in addition to KNO 3 、KNO 2 Besides containing less than 10 mass% of NaNO 3 And the molten salt of (2).
The chemical strengthening treatment conditions for forming a desired surface compressive stress in a glass plate are different depending on the plate thickness of the glass plate, and the conditions are typical in which the glass plate is immersed in a molten salt such as a potassium nitrate molten salt at 350 to 550 ℃ for 2 to 50 hours. From the economical point of view, the glass plate is preferably immersed at 350 to 500 ℃ for 2 to 40 hours, more preferably 2 to 30 hours.
In the slow cooling step, the glass plate taken out of the molten salt is slowly cooled. The glass sheet taken out of the molten salt is preferably not cooled slowly as it is, but is maintained at a uniform temperature for a certain period of time so that a temperature distribution is less likely to occur on the principal surface of the glass sheet.
The difference between the holding temperature and the temperature of the molten salt is preferably 100 ℃ or less, more preferably 50 ℃ or less, further preferably 20 ℃ or less, and particularly preferably 10 ℃ or less. The holding time is preferably 10 minutes or longer, more preferably 20 minutes or longer, and still more preferably 30 minutes or longer.
The glass sheet taken out of the molten salt is preferably cooled slowly so that the slow cooling rate until the glass sheet reaches 100 ℃ is 300 ℃ per hour or less. The slow cooling rate is more preferably 200 ℃/hr or less, and still more preferably 100 ℃/hr or less.
The chemical strengthening treatment step may be performed after chamfering the end face 12, and the end face 12 may be chamfered after the chemical strengthening treatment step, or the end face 12 may not be chamfered.
The chemical strengthening treatment step may be followed by a cutting step of cutting the chemically strengthened glass plate. By having a cutting process after the chemical strengthening treatment process, productivity is improved. By cutting the glass plate after the chemical strengthening treatment process, a glass plate in which the surface compressive stress caused by the chemical strengthening treatment is not formed on the end face 12 can be obtained.
In the cutting step, the glass sheet may be cut by cutting after scribing with a thermal stress using a laser or a gas burner. By cutting the glass sheet after thermal stress scoring, microcracks are less likely to occur. In addition, scattering of the laser beam in the end face strengthening process can be reduced.
In the end face strengthening step, a planar compressive stress is formed in a direction parallel to the end face along the end face of the glass plate having the surface compressive stress formed on the main surface in the chemical strengthening treatment step.
Fig. 4 is a cross-sectional view of the tempered glass sheet when the laser beam is irradiated in the end surface tempering process.
In the end face strengthening step, the inside of the glass plate 10 is heated by, for example, irradiating the end face 12 of the glass plate with a laser beam 60. Then, the inside of the glass plate 10 cools down slower than the end face 12 of the glass plate 10, thereby generating a tensile stress in the inside of the glass plate 10. At this time, by equalizing the stress, a compressive stress region corresponding to a tensile stress region generated in the glass plate 10 is formed in the end face 12 of the glass plate, and the end face 12 can be reinforced.
In the end face strengthening step, the glass sheet 10 is heated so that the temperature T1 of the glass sheet 10 is equal to or greater than the strain point of the glass sheet 10 at a position D at which the length from the end face in the direction normal to the end face is equal to the thickness of the glass sheet 10 when the laser beam 60 is irradiated. If the temperature T1 at the position D is equal to or higher than the strain point of the glass sheet 10, the end face 12 can be sufficiently strengthened.
In the end face strengthening process, when the laser beam 60 is irradiated, the temperature T2 of the end face 12 of the glass plate 10 is less than the softening point of the glass plate 10, and T1 > T2. If the temperature of the end face 12 is less than the softening point of the glass sheet 10 and T1 > T2, no tensile stress is generated at the surface of the end face 12 thereafter. Given that the temperature of the end face 12 is T1 < T2, a tensile stress may then be generated at a portion of the surface of the end face 12. When the temperature of the end face 12 is equal to or higher than the softening point, the end face is deformed. When the laser beam 60 is irradiated, the temperature T2 of the end face 12 of the glass plate 10 is preferably equal to or lower than the annealing point of the glass plate 10, and more preferably equal to or lower than the strain point of the glass plate 10.
In the end face strengthening step, the temperature of the first main face 11a and the second main face 11b of the glass plate 10 is preferably 300 ℃ or lower when the laser beam 60 is irradiated. If the temperature of the first main surface 11a and the second main surface 11b of the glass plate 10 is 300 ℃ or lower, deformation of the glass plate 10 can be suppressed. In addition, the diffusion of ions can be suppressed, and the decrease in the strength of the first main surface 11a and the second main surface 11b can be suppressed. When the laser beam 60 is irradiated, the temperature of the first main surface 11a and the second main surface 11b of the glass plate 10 is more preferably 200 ℃ or less, and still more preferably 100 ℃ or less.
In the end surface strengthening step, the laser beam 60 is made incident into the glass plate 10 from the end surface 12 of the glass plate 10, whereby the inside of the glass plate 10 can be heated in a wide range, and strengthening of the end surface 12 can be promoted.
The laser beam 60 is preferably focused inside the glass plate 10 while being irradiated onto the end face 12 of the glass plate 10. By disposing the converging point 21 of the laser beam 60 inside the glass plate 10, the inside of the glass plate 10 is higher than the surface temperature of the glass plate 10.
The laser beam 60 primarily produces linear absorption by irradiation of the glass sheet 10. By primarily producing linear absorption is meant that the amount of heat produced by linear absorption is greater than the amount of heat produced by nonlinear absorption. Non-linear absorption may hardly occur.
Nonlinear absorption is also known as multiphoton absorption. The probability of occurrence of multiphoton absorption is nonlinear with respect to photon density (power density of the laser beam 60), and the probability becomes significantly higher as photon density becomes higher. For example, the probability of two-photon absorption occurring is proportional to the square of the photon density.
According to the findings of the present inventors, etc., in the case of the glass plate 10, in order to generate effective nonlinear absorption so that tensile stress is generated inside the glass plate 10, the photon density is preferably 1×10 8 W/cm 2 The above.
At any location of the glass sheet 10, the photon density may be less than 1 x 10 8 W/cm 2 . In this case, nonlinear absorption hardly occurs. Since the size of the cross section of the laser beam 60 is larger than the wavelength, the size of the focal spot 21 is not zero, and the photon density at the focal spot can be less than 1×10 8 W/cm 2 。
On the other hand, linear absorption is also referred to as single photon absorption. The probability of single photon absorption occurring is proportional to the photon density. In the case of single photon absorption, the intensity of the laser beam 60 decays according to Lambert-Beer's law.
When the laser beam 60 is moved a distance E (unit [ cm ]]) During which the intensity of the laser beam 60 is from I 0 When changing to I, i=i 0 The formula of x exp (- α×e) holds. Alpha is the absorption coefficient (unit [ cm ] -1 ]) Is measured by an ultraviolet-visible near-infrared spectrophotometer or the like.
The absorption coefficient α may be, for example, less than 100. When the absorption coefficient α is 100 or more, most of the laser beam 60 is absorbed near the surface of the glass plate 10, and it is difficult to heat the inside of the glass plate 10. The absorption coefficient α is preferably less than 30, more preferably less than 10. The absorption coefficient alpha is typically greater than 0. The absorption coefficient α depends on the wavelength of the laser beam 60, the glass composition of the glass sheet 10, and the like. It is preferable to irradiate a laser beam having a wavelength with an absorption coefficient α smaller than 100.
The wavelength of the laser beam 60 depends on the glass composition of the glass plate 10 and the like, and may be, for example, 250nm to 5000nm. When the wavelength of the laser beam 60 is 250nm to 5000nm, the absorption coefficient α is converged within an appropriate range.
Examples of the light source of the laser beam 60 include: yb fiber laser (wavelength: 1000 nm-1100 nm), yb disk laser (wavelength: 1000 nm-1100 nm), nd: YAG laser (wavelength: 1064 nm), high power semiconductor laser (wavelength: 808 nm-980 nm), and the like.
As a light source of the laser beam 60, a UV laser (wavelength: 355 nm), a green laser (wavelength: 532 nm), or Ho: YAG laser (wavelength: 2080 nm), er: YAG lasers (2940 nm), lasers using mid-infrared parametric oscillators (wavelengths: 2600nm to 3450 nm), and the like.
The light source of the laser beam 60 may be of a pulsed oscillation type, preferably a continuous oscillation type. In the case of continuous oscillation, the inside of the glass plate 10 can be heated over a wide range.
The number of laser beams 60 may be one or a plurality of laser beams 60 in fig. 4, and a plurality of laser beams 60 may be simultaneously irradiated onto the glass sheet 10.
In the end face strengthening step, the laser beam 60 is irradiated to the glass plate 10 to mainly generate linear absorption, and the inside of the glass plate 10 is heated to a temperature higher than the end face 12 of the glass plate 10 to form tensile stress, whereby the end face 12 of the glass plate 10 is strengthened. By mainly generating linear absorption, the inside of the glass plate 10 can be heated over a wide range, and strengthening of the end face 12 can be promoted, as compared with the case where nonlinear absorption is mainly generated. In addition, by heating the inside of the glass sheet 10 to a temperature higher than the end face 12 of the glass sheet 10, a plane tensile stress is less likely to occur in the reinforcing portion 30, and thermal cracking of the glass sheet 10 starting from the heated portion can be suppressed.
In the end surface strengthening step, the strengthening portion 30 is formed on the outer edge of the glass plate 10 by moving the irradiation position of the laser beam 60 along the end surface 12 of the glass plate 10. The reinforcement portion 30 may be formed continuously along at least a part of the outer edge of the glass sheet 10, or may be formed integrally along the outer edge of the glass sheet 10.
The movement of the irradiation position of the laser beam 60 in the glass plate 10 is performed by the movement of the glass plate 10, the light source of the laser beam 60, or both. The movement of the irradiation position of the laser beam 60 in the glass plate 10 can also be performed by the operation of the galvanometer mirror.
The irradiation start position of the laser beam 60 is preferably the following position: the center of the irradiation shape of the laser beam 60 on the end face 12 of the glass plate 10 is located further inside than the end of the glass plate 10 on the end face 12 of the glass plate 10. By the irradiation start position of the laser beam 60 being a position further inside than the end portion of the glass plate 10, the glass plate 10 is less likely to be broken and the manufacturing equipment is less likely to burn.
The irradiation shape of the laser beam 60 on the end face 12 of the glass plate 10 may be formed in a linear shape along the moving direction of the laser beam 60 in the glass plate 10. At this time, the power distribution in the moving direction of the laser beam 60 in the glass plate 10 may be a top hat distribution or a gaussian distribution. By forming the glass plate 10 in a linear shape, the temperature change of the glass plate 10 is reduced, and thermal cracking of the glass plate 10 in the end surface strengthening process can be suppressed.
The width Φ (see fig. 4) of the irradiation shape of the laser beam 60 on the end face 12 of the glass plate 10 in the plate thickness direction may be equal to or smaller than the thickness of the glass plate 10. By forming the width Φ in the plate thickness direction of the irradiation shape of the laser beam 60 on the end face 12 of the glass plate 10 to be equal to or smaller than the thickness of the glass plate 10, it is possible to suppress heating of the main faces 11a, 11b in the vicinity of the end face 12 and to suppress reduction in the surface compressive stress formed by the chemical strengthening treatment in the main faces 11a, 11b in the vicinity of the end face 12.
The power distribution center position in the plate thickness direction of the laser beam 60 in the glass plate 10 may coincide with the plate thickness center. By matching the plate thickness center, the end face strengthening process can be effectively performed. In addition, by matching the center of the plate thickness, the glass plate 10 is less likely to warp after the end surface strengthening. Here, the coincidence with the plate thickness center means that the power distribution center position of the laser beam 60 in the plate thickness direction may coincide with the plate thickness center, may be deviated from the plate thickness center by ±30% of the plate thickness, or may be deviated from the plate thickness center by ±15% of the plate thickness. In order to control the power distribution center position in the plate thickness direction of the laser beam 60 to coincide with the plate thickness center, for example, the surface of the glass plate 10 may be measured using a distance sensor.
When the laser beam 60 is irradiated onto the end face 12 of the glass plate 10, the principal surface of the glass plate 10 is preferably restrained by a jig or the like. By restraining the principal surface of the glass sheet 10, even if the glass sheet 10 expands due to the irradiation of the laser beam 60, deformation can be suppressed, and the laser beam 60 can be irradiated to a desired position of the glass sheet 10 without the glass sheet 10 being deviated from the irradiation position of the laser beam 60. The entire main surface of the glass sheet 10 is preferably restrained by a jig, but a part of the main surface of the glass sheet 10 may be restrained. In the case of restraining a part of the principal surface of the glass plate 10, the jigs are preferably provided at a constant interval on the principal surface of the glass plate 10, and may be at an interval of 250mm or less.
In addition, it is preferable to use a material having a small thermal conductivity at a portion in contact with the glass plate 10. By using a material having a small thermal conductivity, thermal stress is less likely to occur at the contact portion of the surface of the glass plate 10, and the glass plate 10 is less likely to break. Examples of the material having a small thermal conductivity include MC nylon and fluorine-containing resin.
The intensity and the moving speed of the laser beam 60 are preferably determined on the basis of the absorption coefficient α of the glass sheet 10 determined in advance. The greater the absorption coefficient α, the weaker the intensity of the laser beam 60, and the faster the movement speed is preferably set. When the intensity of the laser beam 60 is too strong, the glass plate 10 is easily broken.
In the end face strengthening step, a gas such as compressed air or a liquid such as mist may be blown onto the glass sheet 10, or a mixture thereof. This can suppress the temperature rise of the surface of the glass plate 10. In addition, this can ensure a temperature difference between the surface of the glass plate 10 and the inside of the glass plate 10, and can alleviate the irradiation condition of the laser beam 60. In addition, foreign matter such as dust adhering to the surface of the glass plate 10 can be removed. When the laser beam 60 is irradiated onto the foreign matter, the foreign matter absorbs the laser beam 60.
The protective layer may be formed on the end face 12 after the end face reinforcing step.
In the tempered glass sheet of the present embodiment described above, the strength of both the main surface and the end surface is high, and breakage is not easily caused.
The present invention is not limited to the above embodiments. Variations, modifications, and the like within a range that can achieve the object of the present invention are included in the present invention.
In the above embodiment, the embodiment has been described as a mode in which the inside of the glass sheet 10 is heated by irradiating the laser beam 60 to the end face 12 of the glass sheet in the end face strengthening step, but the end face 12 may be strengthened by heating the inside of the glass sheet 10 with an infrared heater or microwaves.
Examples
The present invention will be specifically described below with reference to examples, but the present invention is not limited to these examples.
Fig. 5 is a cross-sectional view showing a tempered glass plate 200 of an embodiment.
Examples 1, 3 and 5 are examples, and examples 2, 4 and 6 are comparative examples.
Various glass raw materials such as silica sand were prepared into glass compositions shown in table 1, and melted at a temperature of 1400 to 1500 ℃, and the obtained molten glass was formed into a plate shape by a float method so as to have a thickness T shown in table 2, and then cut, thereby obtaining a rectangular glass plate.
The glass transition temperature Tg (unit: DEG C), specific gravity, young's modulus (unit: GPa), and average thermal expansion coefficient (unit: 10) of the obtained glass plate -7 /DEG C). The results are shown in Table 1.
Hereinafter, a method for measuring each physical property of the glass plate is described.
(glass transition temperature Tg)
The measurement was performed by using a differential thermal expansion meter (TMA) according to the method specified in JIS R3103-3 (2001).
(specific gravity)
About 20g of glass gob free of bubbles was measured by archimedes' method.
(Young's modulus)
The measurement was performed by an ultrasonic pulse method.
(average coefficient of thermal expansion)
The measurement was performed by using a differential thermal expansion meter (TMA) according to the method specified in JIS R3102 (1995). The measurement temperature range is 50-350 ℃.
Example 1
The obtained glass plate was cut into a short side having a length a and a long side having a length b shown in table 2 by a wheel chopper, and C-chamfered. The glass plate after chamfering was immersed in a molten potassium nitrate salt, and a strengthened glass plate was obtained by chemical strengthening treatment. CS and DOL of the main surface of the obtained tempered glass plate were measured. CS and DOL were calculated from the number of interference fringes and the interval observed using a surface stress meter (manufactured by folding primitive manufacturing: FSM-7000H). In the calculation, the refractive index of the tempered glass plate was set to 1.518, and the optical elastic constant was set to 27.1[ (nm/cm)/MPa ]. The results of CS and DOL on the main surface are shown in table 2.
As shown in fig. 5, the end face 212 of the obtained tempered glass sheet 200 is directed upward, the principal surface 211 of the glass sheet is fixed by a jig, and a laser beam 260 is irradiated onto the end face 212 from above in the vertical direction so as to be condensed inside the tempered glass sheet 200, whereby a tempered portion having a plane compressive stress along the end face 212 is formed.
As a light source of the laser beam 260, a fiber laser of a wavelength (1070 nm) generating linear absorption is mainly used. The irradiation position of the laser beam 260 was set at the center of the end face 212 of the tempered glass sheet 200 in the sheet thickness direction, and the sheet was moved in the longitudinal direction of the tempered glass sheet 200 at a movement speed of 10.0 mm/sec. The irradiation shape of the laser beam 260 on the end face 212 of the glass plate 200 was set to have a width of 2mm and a length of 100mm. The center of the irradiation shape of the laser beam 260 in the end face 212 of the glass plate 200 is positioned further inside than the end of the glass plate 200 on the end face 212 of the glass plate 200.
The depth f (see fig. 5) of the converging point in the width direction of the tempered glass plate 200 from the end face 212 was set to 56.8mm, and the output power P (not shown) of the light source of the laser beam 260 was set to 1300W. The absorption coefficient of the glass plate was 0.57[1/cm ].
By irradiating the laser beam 260, the temperature at the position D of the tempered glass sheet 200, which is the same length as the thickness of the tempered glass sheet 200 from the end face 212 in the normal direction of the end face 212, is equal to or higher than the strain point of the tempered glass sheet 200. The temperature of the end face 212 of the glass plate 10 was 607 ℃. Since the softening point of the glass sheet 10 is 730 ℃, the temperature of the end face 212 is less than the softening point, and T1 > T2.
The maximum value of the plane compressive stress of the strengthened portion of the strengthened glass plate 200 of example 1 was 22.1MPa, and the width C of the strengthened portion from the end face 212 was 2.7mm. The width C is 0.5 times or more the thickness T of the glass plate 200. In addition, no plane tensile stress is formed in the reinforcing portion. The plane compressive stress of the reinforcing portion was measured by a birefringent two-dimensional distribution evaluation device (WPA-100 manufactured by Photonic Lattice Co., ltd.).
15 tempered glass plates 200 were produced by the above method, and the 4-point bending strength of 15 tempered glass plates 200, in which the end face 212 irradiated with the laser beam 260 was downward, was measured for the bent strength of the tempered glass plates 200 at the point where the bent shape was convex. The obtained values were averaged to obtain an average fracture stress. Further, weibull coefficients were obtained by Weibull plotting according to JIS R1625 (1996). The upper span was set to 20mm, the lower span was set to 60mm, and the crosshead speed was set to 1 mm/min. As a result, the average fracture stress was 346MPa. Further, the 0.1% fracture probability strength obtained assuming that the logarithmic value of the fracture stress is a normal distribution was 259MPa, and the weibull coefficient was 12.3.
Example 2
18 tempered glass plates 200 were produced in the same manner as in example 1, but no laser beam 260 was irradiated to the end face 212. A4-point bending test was performed in the same manner as in example 1. As a result, the maximum value of the plane compressive stress of the reinforcing portion was 1.9MPa, and the width C of the reinforcing portion from the end face 212 was 0.77mm. The width C is less than 0.5 times the thickness T of the glass sheet 200. The average breaking stress was 311MPa. Further, the 0.1% fracture probability strength obtained assuming that the logarithmic value of the fracture stress is a normal distribution was 122MPa, and the weibull coefficient was 3.6.
The weibull diagrams of examples 1 and 2 are shown in fig. 6. When comparing the results of the 4-point bending test of examples 1 and 2, the average breaking stress and weibull coefficient of example 1 in which the end face was irradiated with the laser beam were larger than those of example 2 in which the end face was not irradiated with the laser beam. The 0.1% fracture probability intensity obtained assuming that the logarithmic value of the fracture stress of example 1, in which the laser beam was irradiated to the end face, was a normal distribution was larger than the 0.1% fracture probability intensity obtained assuming that the logarithmic value of the bending intensity of example 2, in which the laser beam was not irradiated to the end face, was a normal distribution. It is found that the end face can be reinforced by irradiating the end face with a laser beam to form a reinforcing portion on the end face.
Example 3
A rectangular glass plate was obtained by forming the glass plate into a plate shape by the float method in the same manner as in example 1. The obtained glass plate was immersed in a molten potassium nitrate salt, and a chemically strengthened glass plate was obtained by performing a chemical strengthening treatment. The obtained tempered glass plate was cut into a short side having a length a and a long side having a length b shown in table 2 by a wheel chopper, and subjected to C chamfering. CS and DOL of the tempered glass plate after chamfering were measured. The results are shown in table 2.
Next, the end face of the tempered glass sheet 200 was irradiated with the laser beam 260 in the same manner as in example 1, the depth f (see fig. 5) of the converging point in the width direction from the end face 212 was set to 30mm, and the output P of the light source of the laser beam 260 was set to 1600W.
The maximum value of the plane compressive stress of the strengthened portion of the strengthened glass plate 200 of example 3 was 62.7MPa, and the width C of the strengthened portion from the end face 212 was 3.0mm. The width C is 0.5 times or more the thickness T of the tempered glass plate 200. In addition, no plane tensile stress is formed in the reinforcing portion.
A4-point bending test was conducted in the same manner as in example 1, and as a result, the average breaking stress was 208MPa. Further, the 0.1% fracture probability strength obtained assuming that the logarithmic value of the fracture stress is a normal distribution was 159MPa.
Example 4
19 tempered glass plates were produced in the same manner as in example 3, and the end face 212 was not irradiated with the laser beam 260. A4-point bending test was performed in the same manner as in example 3. As a result, the maximum value of the plane compressive stress of the reinforcing portion was 2.1MPa, and the width C of the reinforcing portion from the end face 212 was 0.52mm. The width C is less than 0.5 times the thickness T of the tempered glass sheet 200. In addition, the average fracture should be 84MPa. Further, the 0.1% fracture probability strength obtained assuming that the logarithmic value of the fracture stress is a normal distribution was 66MPa.
In comparing the results of the 4-point bending test of examples 3 and 4, the average breaking stress of example 3 in which the end face was irradiated with the laser beam was larger than the average breaking stress of example 4 in which the end face was not irradiated with the laser beam. The 0.1% fracture probability intensity obtained assuming that the logarithmic value of the fracture stress of example 3 in which the laser beam was irradiated to the end face was a normal distribution was larger than the 0.1% fracture probability intensity obtained assuming that the logarithmic value of the bending intensity of example 4 in which the laser beam was not irradiated to the end face was a normal distribution. It is found that the end face can be reinforced by irradiating the end face with a laser beam to form a reinforcing portion on the end face.
Example 5
A tempered glass plate was obtained in the same manner as in example 1. The obtained tempered glass plate was subjected to thermal stress scribing by a laser so that the length of the short side was a and the length of the long side was b as shown in table 2, and then cut to obtain a 10-mirror-surface C-chamfered tempered glass plate. The end face 212 of the obtained tempered glass plate is directed upward, and the principal surface 211 of the glass plate is fixed by a jig, and the end face 212 is irradiated with a laser beam 260 from above perpendicularly, whereby a tempered portion having a planar compressive stress is formed on the end face 212.
As a light source of the laser beam 260, a fiber laser of a wavelength (1070 nm) generating linear absorption is mainly used. The irradiation position of the laser beam 260 was set at the center of the end face 212 of the glass plate 200 in the plate thickness direction, and the glass plate 200 was moved in the longitudinal direction at a movement speed of 10.0 mm/sec. The irradiation shape of the laser beam 260 on the end face 212 of the tempered glass sheet 200 was set to have a width of 2mm and a length of 100mm. The irradiation start position of the laser beam 260 is a position at which the center of the irradiation shape of the laser beam 60 on the end face 12 of the glass plate 10 is located further inside than the end of the glass plate 10 on the end face 12 of the glass plate 10.
The depth f (see fig. 5) of the converging point in the width direction of the tempered glass plate 200 from the end face 212 was set to 30mm, and the output power P (not shown) of the light source of the laser beam 260 was set to 1550W. The absorption coefficient of the glass plate was 0.57[1/cm ].
By irradiation with the laser beam 260, the temperature at the position D of the tempered glass sheet 200, which is the same length as the thickness of the glass sheet 200 from the end face 212 in the normal direction of the end face 212, is equal to or higher than the strain point of the tempered glass sheet 200. The temperature of the end face 212 of the tempered glass plate 200 was 532 ℃. Since the softening point of the glass sheet 10 is 730 ℃, it is smaller than the softening point, and T1 > T2.
The maximum value of the plane compressive stress of the strengthened portion of the strengthened glass plate 200 of example 5 was 2.8MPa, and the thickness C of the strengthened portion from the end face 212 was 8mm, which was 2.85 times the thickness T (2.8 mm) of the glass plate 200. In addition, no plane tensile stress is formed in the reinforcement portion. The plane compressive stress of the reinforcing portion was measured by a birefringent two-dimensional distribution evaluation device (WPA-100 manufactured by Photonic Lattice Co., ltd.).
After the irradiation of the laser beam 260, a transparent adhesive tape (manufactured by Nitoms corporation, J6150) was attached as a protective layer to the end face 212 irradiated with the laser beam 260, and then a 4-point bending test was performed to bend and deform the glass plate 200 downward into a convex shape. The upper span was set to 300mm, the lower span was set to 900mm, and the crosshead speed was set to 1 mm/min. As a result, the average breaking stress was 458MPa. Further, the 0.1% fracture probability strength obtained assuming that the logarithmic value of the fracture stress is normally distributed was 329MPa, and the weibull coefficient was 20.65.
Example 6
16 tempered glass plates were produced in the same manner as in example 5, but the end face 212 was not irradiated with the laser beam 260. A4-point bending test was performed in the same manner as in example 5. As a result, the average fracture stress was 324MPa. Further, the 0.1% fracture probability strength obtained assuming that the logarithmic value of the fracture stress is a normal distribution was 46.9MPa, and the weibull coefficient was 2.63.
In comparing the results of the 4-point bending test of examples 5 and 6, the average breaking stress and weibull coefficient of the bending strength of example 5 in which the end face was irradiated with the laser beam were larger than those of example 6 in which the end face was not irradiated with the laser beam. The 0.1% fracture probability intensity obtained assuming that the logarithmic value of the fracture stress of example 5, in which the laser beam was irradiated to the end face, was a normal distribution was larger than the 0.1% fracture probability intensity obtained assuming that the logarithmic value of the bending intensity of example 6, in which the laser beam was not irradiated to the end face, was a normal distribution. It is known that the end face can be reinforced by irradiating the end face with a laser beam to form a reinforcing portion on the end face.
From the above results, it was found that the end face of the glass plate can be strengthened by irradiating the end face with a laser beam to form a strengthening portion along the end face. Although the detailed reason for improving the breaking stress by forming the reinforcing portion on the end face is not clear, it is considered that not only the strength is improved by the stress, but also the strength is improved by repairing the damage generated on the end face of the glass plate.
TABLE 1
TABLE 2
| Example 1 | Example 2 | Example 3 | Example 4 | Example 5 | Example 6 | |
| Length of short side of glass plate a (mm) | 15 | 15 | 15 | 15 | 100 | 100 |
| Length b (mm) of long side of glass plate | 70 | 70 | 70 | 70 | 1000 | 1000 |
| Thickness T (mm) of glass plate | 2.8 | 2.8 | 1.8 | 1.8 | 2.8 | 2.8 |
| CS(MPa) | 561 | 561 | 664 | 664 | 465 | 465 |
| DOL(μm) | 10.0 | 10.0 | 9.4 | 9.4 | 15.9 | 15.9 |
| Maximum value of plane compressive stress (MPa) of reinforcement portion | 22.1 | 1.9 | 62.7 | 2.1 | 2.8 | 1.3 |
| Width C (mm) from end face of reinforcing part | 2.7 | 0.77 | 3.0 | 0.52 | 8.0 | 1.1 |
| Average breaking stress (MPa) | 346 | 311 | 208 | 84 | 458 | 324 |
| Log 0.1% fracture probability (MPa) | 259 | 122 | 159 | 66 | 329 | 46.9 |
| Weibull coefficient | 12.3 | 3.6 | – | – | 20.65 | 2.63 |
While the invention has been described in detail and with reference to specific embodiments thereof, it will be apparent to one skilled in the art that various changes and modifications can be made therein without departing from the spirit and scope thereof. The present application is based on japanese patent application (japanese patent application publication No. 2019-120489) filed on 27 at 6/2019, the contents of which are incorporated herein by reference.
Industrial applicability
The tempered glass sheet of the present invention is suitable for use as, for example, a building window, an outer wall, a handrail material, a solar cell protective glass, a vehicle window.
Description of the reference numerals
10 reinforced glass plate
11a first main face
11b second main face
12 end face
30 strengthening portion
Claims (18)
1. A tempered glass sheet having a first main surface, a second main surface opposite to the first main surface, and an end surface, wherein,
at least one of the first major face and the second major face has a surface compressive stress formed by a chemical strengthening treatment,
the tempered glass plate has a tempered portion in which a planar compressive stress is formed along the end face in a direction parallel to the end face,
The maximum value of the plane compressive stress of the reinforcement part is 1MPa to 120MPa,
the width of the reinforcing part from the end face in the normal direction of the end face is 0.5 times or more the thickness of the reinforced glass plate, and
the plate thickness of the reinforced glass plate is more than 0.5 mm.
2. The tempered glass sheet as claimed in claim 1, wherein CS of the surface compressive stress is 200MPa or more.
3. A tempered glass sheet as claimed in claim 1 or 2, wherein the DOL of the surface compressive stress is 5 μm or more.
4. The tempered glass sheet according to claim 1 or 2, wherein surface compressive stress generated by a chemical strengthening treatment is not formed on the end face having the strengthening portion.
5. A tempered glass sheet as claimed in claim 1 or 2 wherein the strengthening portion has no planar tensile stress.
6. A tempered glass plate as claimed in claim 1 or 2, wherein a protective layer is provided on the end face having the strengthening portion.
7. The tempered glass sheet as claimed in claim 1 or 2, wherein the tempered glass sheet contains, in mole percent on an oxide basis: 0.003 to 1.5 percent of Fe 2 O 3 56-75% of SiO 2 0 to 20 percent of Al 2 O 3 8 to 22 percent of Na 2 O, 0-10% of K 2 O, mgO of 0-14% and ZrO of 0-5% 2 And 0 to 12% CaO.
8. A tempered glass plate as claimed in claim 1 or 2, wherein the strengthening portion is formed at the following positions on the end face:
the distance between the corner where the adjacent end surfaces contact each other is 1.0 to 10 times the thickness of the tempered glass plate.
9. The tempered glass sheet according to claim 1 or 2, wherein a planar tensile stress is formed in a direction parallel to the end face at a position on the tempered portion adjacent to an opposite side of the end face.
10. The tempered glass sheet as claimed in claim 1 or 2, wherein the whole of the tempered glass sheet has a uniform specific gravity.
11. A tempered glass sheet as claimed in claim 1 or 2, wherein a chamfer is provided at a boundary portion of the end face and the first main face and a boundary portion of the end face and the second main face, respectively.
12. A method for producing a tempered glass sheet, which is the method for producing a tempered glass sheet according to any one of claims 1 to 11, wherein the method for producing a tempered glass sheet comprises:
A chemical strengthening treatment step in which at least one main surface of a glass sheet is immersed in a molten salt, thereby forming a surface compressive stress on the main surface of the glass sheet; and
an end face strengthening step of forming a plane compressive stress along an end face of the glass plate in a direction parallel to the end face after the chemical strengthening treatment step, and
in the end face strengthening process, the glass plate is heated so that:
the temperature T1 of the glass plate at a position above the strain point of the glass plate, the temperature T2 of the end face being less than the softening point of the glass plate and T1 > T2,
the position is a position at which a length from the end face in a normal direction of the end face is the same as a thickness of the tempered glass sheet.
13. The method for producing a reinforced glass sheet according to claim 12, wherein in the end face reinforcing step, a planar compressive stress is formed on the end face of the glass sheet by irradiation of a laser beam.
14. The method for producing a tempered glass sheet as claimed in claim 13, wherein in the end surface tempering step, irradiation is performed such that an absorption coefficient α of the glass sheet is less than 100[ cm ] -1 ]Is provided, the laser beam having a wavelength of (a).
15. The method for producing a tempered glass sheet as claimed in claim 13 or 14, wherein in the end surface tempering step, the wavelength of the laser beam is 250nm to 5000nm.
16. The method for producing a tempered glass sheet according to any one of claims 12 to 14, wherein the step of chemically strengthening is followed by a step of cutting the glass sheet after the step of chemically strengthening.
17. The method for manufacturing a tempered glass sheet as claimed in claim 16, wherein in the cutting step, the glass sheet is cut by a method using thermal stress scoring.
18. The method for producing a tempered glass sheet according to any one of claims 12 to 14 and 17, wherein a protective layer is formed on the end face after the end face tempering step.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2019-120489 | 2019-06-27 | ||
| JP2019120489 | 2019-06-27 | ||
| PCT/JP2020/024383 WO2020262293A1 (en) | 2019-06-27 | 2020-06-22 | Tempered glass plate and method for producing same |
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| CN114096490A CN114096490A (en) | 2022-02-25 |
| CN114096490B true CN114096490B (en) | 2023-12-19 |
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| US (1) | US20220112126A1 (en) |
| JP (1) | JPWO2020262293A1 (en) |
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- 2020-06-22 CN CN202080046654.1A patent/CN114096490B/en active Active
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| JPWO2020262293A1 (en) | 2020-12-30 |
| US20220112126A1 (en) | 2022-04-14 |
| WO2020262293A1 (en) | 2020-12-30 |
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